EP2341161A1 - Tuyau en acier inoxydable à haute limite élastique présentant une résistance élevée à la corrosion fissurante en présence d'hydrogène sulfuré et une résistance à la corrosion en présence de dioxyde de carbone à haute température - Google Patents

Tuyau en acier inoxydable à haute limite élastique présentant une résistance élevée à la corrosion fissurante en présence d'hydrogène sulfuré et une résistance à la corrosion en présence de dioxyde de carbone à haute température Download PDF

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Publication number
EP2341161A1
EP2341161A1 EP09823629A EP09823629A EP2341161A1 EP 2341161 A1 EP2341161 A1 EP 2341161A1 EP 09823629 A EP09823629 A EP 09823629A EP 09823629 A EP09823629 A EP 09823629A EP 2341161 A1 EP2341161 A1 EP 2341161A1
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Prior art keywords
less
stainless steel
content
phase
steel pipe
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EP09823629A
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German (de)
English (en)
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EP2341161B1 (fr
EP2341161A4 (fr
Inventor
Kunio Kondo
Hisashi Amaya
Hideki Takabe
Taro Ohe
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Nippon Steel Corp
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Sumitomo Metal Industries Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten

Definitions

  • the present invention relates to a stainless steel pipe having a high strength, in particular, a stainless steel pipe or a line pipe for use in oil well, used for oil well producing crude oil or gas well producing natural gas; in particular, the present invention relates to a stainless steel pipe having an excellent corrosion resistance and a high strength, suitable for use in oil well or gas well in a severe high-temperature corrosive environment containing hydrogen sulfide gas, carbonic acid gas and chloride ions.
  • oil wells and gas wells in environments containing carbonic acid gas, it has been common to use 13% Cr martensitic stainless steel pipes excellent in carbonic-acid gas corrosion resistance.
  • oil wells recent increasing depth of oil wells and gas wells (hereinafter, abbreviated as oil wells) requires materials higher in strength than has hitherto been required.
  • the oil well environment is such that as the depth of the oil well is increased, the environment becomes higher in temperature and pressure, and higher in the partial pressures of carbonic acid gas and hydrogen sulfide. Therefore, steel pipes having sufficient corrosion resistance even in severer environments come to be needed.
  • the present inventors have investigated the component composition of a stainless steel which simultaneously satisfies the above-described three conditions (high strength, sufficient corrosion resistance in a high-temperature carbonic acid gas environment, sufficient sulfide stress cracking resistance). Specifically, first, for the purpose of being capable of ensuring sufficient corrosion resistance even in a carbonic acid gas environment at a high temperature (for example, 200°C), the investigation of the alloy composition of the stainless steel has been performed. Consequently, it has been discovered that the content of Cr is most important for the purpose of ensuring the corrosion resistance of stainless steel. Additionally, the present inventors have also discovered that it is necessary to contain a certain amount of Mo in the stainless steel for the purpose of ensuring sufficient sulfide stress cracking resistance.
  • the present inventors have investigated the component system of a stainless steel capable of satisfying the strength, toughness and corrosion resistance although the component system is not a martensitic single-phase system. Specifically, ⁇ -ferrite was positively utilized, and on the basis of ⁇ -ferrite, investigation was made on the ensuring of a strength as high as conventional strengths and on the further improvement of the corrosion resistance. Consequently, it has been revealed that by utilizing the precipitation strengthening effect through the addition of Cu, the strength can be ensured and additionally the corrosion resistance is also improved.
  • Ni is also an element that improves the corrosion resistance, and addition of a larger amount of Ni can improve the corrosion resistance; however, the addition of a larger amount of Ni decreases the Ms point, namely, the martensitic transformation point temperature. Consequently, the retained ⁇ -phase becomes larger in proportion and is stabilized, and hence the strength of the stainless steel is drastically deteriorated. Therefore, the present inventors have made various investigations on the basis of the idea that if the deterioration of the strength can be suppressed by increasing the Ms point, Ni can be effectively utilized.
  • an object of the present invention is to provide a stainless steel pipe which has a high strength that can cope with very deep oil well or gas well, has a sufficient corrosion resistance even in a carbonic acid gas environment at a temperature as high as 200°C, and has a sufficient sulfide stress cracking resistance even when the environmental temperature of the oil well or the gas well is decreased by temporal suspension of the collection of crude oil or gas.
  • the statement that "a sufficient corrosion resistance is maintained even in a high-temperature carbonic acid gas environment” means the fact that in a high-temperature carbonic acid gas environment containing chloride ions, an excellent corrosion resistance is exhibited against the stress corrosion cracking. Specifically, the statement means that even in such a severe environment that the temperature is about 200°C, a corrosion resistance capable of suppressing the occurrence of the stress corrosion cracking is maintained.
  • a high-strength stainless steel pipe refers to a high-strength stainless steel pipe having a yield strength of 758 MPa (110 ksi) or more and more preferably 861 MPa (125 ksi) or more.
  • the present inventors have performed an investigation on the alloy composition of stainless steel for the purpose of ensuring a sufficient corrosion resistance of a stainless steel pipe even in a carbonic acid gas environment at a high-temperature (for example, 200°C). Consequently, the present inventors have discovered that the content of Cr is most important for the purpose of ensuring the corrosion resistance of stainless steel and the content of Cr is required to exceed 16%.
  • Ni in a material (stainless steel) of a component system having a content of Cr more than 16%, the effect of other alloying elements has been investigated from the viewpoint of ensuring the strength.
  • Ni in a 13Cr material, Ni usually stabilizes the austenitic phase at high temperatures. The austenitic phase stabilized by Ni at a high temperature is transformed into a martensitic phase by a subsequent heat treatment (cooling treatment). Consequently, a high-strength stainless steel is obtained.
  • the present inventors have discovered that the addition of Cu and Mo further decreases the Ms point, and hence it is necessary to limit the content of N and the content of Mn in the stainless steel for the purpose of ensuring the necessary high strength by increasing the Ms point.
  • the present invention has been perfected on the basis of the above-described findings, and the gist of the present invention is composed of the stainless steel pipes presented in the following (1) to (3).
  • the stainless steel pipes (1) to (3) are referred to as the aspects (1) to (3) of the present invention, respectively. These aspects are collectively referred to as the present invention, as the case may be.
  • a high-strength stainless steel pipe excellent in sulfide stress cracking resistance and high-temperature carbonic-acid gas corrosion resistance characterized in that: the stainless steel pipe consists of, by mass%, C: 0.05% or less, Si: 1.0% or less, P: 0.05% or less, S: less than 0.002%, Cr: more than 16% and 18% or less, Mo: more than 2% and 3% or less, Cu: 1% to 3.5%, Ni: 3% or more and less than 5%, Al: 0.001% to 0.1% and O: 0.01 % or less, Mn: 1% or less and N: 0.05% or less, and Mn and N in the above ranges satisfy formula (1), and the balance being Fe and impurities; and the metal micro-structure of the stainless steel pipe mainly includes a martensitic phase and includes 10 to 40% of a ferritic phase by volume fraction and 10% or less of a retained ⁇ -phase by volume fraction. M ⁇ n ⁇ N - 0.0045 ⁇ ⁇
  • the stainless steel pipe according to (1) characterized in that the stainless steel pipe further comprises, in place of a part of Fe, one or more of Ca: 0.01% or less and B: 0.01 % or less.
  • the stainless steel pipe according to (1) or (2) characterized in that the stainless steel pipe further comprises, in place of a part of Fe, one or more of V: 0.3% or less, Ti: 0.3% or less, Zr: 0.3% or less and Nb: 0.3% or less.
  • a stainless steel pipe having a high strength and additionally being excellent in corrosion resistance can be provided, and the stainless steel pipe enables to perform, at an inexpensive cost, the production of crude oil or natural gas at a position further deeper than conventional positions. Therefore, the present invention is a high-value invention that contributes to stable global supply of energy.
  • the content of C exceeds 0.05%, Cr carbide is precipitated at the time of tempering and hence the corrosion resistance against high-temperature carbonic acid gas is deteriorated. Accordingly, the content of C is set at 0.05% or less. From the viewpoint of the corrosion resistance, it is preferable to reduce the content of C, and the content of C is preferably 0.03% or less. The more preferable content of C is 0.01% or less.
  • Si is an element that functions as a deoxidizer.
  • the content of Si exceeds 1%, the production amount of ferrite is increased, and no intended high strength comes to be obtained. Accordingly, the content of Si is set at 1.0% or less.
  • the preferable content of Si is 0.5% or less.
  • Si is preferably contained in a content of 0.05% or more.
  • P is an element that deteriorates the corrosion resistance against high-temperature carbonic acid gas.
  • the content of P exceeds 0.05%, the corrosion resistance is deteriorated, and hence the content of P is required to be reduced to 0.05% or less.
  • the preferable content of P is 0.025% or less and the more preferable content of P is 0.015% or less.
  • the stainless steel according to the present invention takes, at the time of high-temperature hot working, a two-phase micro-structure composed of ferrite and austenite, and the adverse effect of S on the hot workability is significant. Therefore, for the purpose of obtaining a stainless steel pipe free from surface defects, the content of S is required to be reduced to less than 0.002%. The more preferable content of S is 0.001 % or less.
  • Cr is an element that is necessary for ensuring the corrosion resistance against high-temperature carbonic acid gas.
  • Cr suppresses the stress corrosion cracking in a high-temperature (for example, 200°C) carbonic acid gas environment.
  • the content of Cr more than 16% is required.
  • Cr has a function of increasing the amount of ferrite and deteriorating the strength, and hence it is necessary to impose a constraint on the content of Cr.
  • the content of Cr exceeds 18%, the amount of ferrite is increased to drastically deteriorate the strength of the stainless steel, and hence the content of Cr is set at 18% or less.
  • the preferable lower limit of Cr content is 16.5%, and the preferable upper limit is 17.8%.
  • Mo has a function of increasing the amount of ferrite and deteriorating the strength of the stainless steel, and hence the adding more than 3%of Mo is not preferable. Accordingly, the range of the content of Mo is set to exceed 2% and to be 3% or less.
  • the preferable lower limit of Mo content is 2.2%, and the preferable upper limit is 2.8%.
  • the portion which is austenite at a high temperature (at the time of hot working), is transformed into martensite at normal temperature, and thus, at normal temperature, the stainless steel becomes of a metal micro-structure mainly composed of the martensitic phase and the ferritic phase; however, for the purpose of ensuring the strength targeted by the present invention, the aging precipitation of the Cu phase is important.
  • the range of the content of Cu is set at from 1% to 3.5%.
  • the preferable lower limit of Cu content is 1.5% and the more preferable lower limit is 2.3%.
  • the preferable upper limit of Cu content is 3.2% and the more preferable upper limit is 3.0%.
  • Ni 3% or more and less than 5%
  • Ni is an element capable of improving the strength of stainless steel by stabilizing austenite at high temperatures and by increasing the amount of martensite at normal temperature. Further, Ni has a function of improving the corrosion resistance in a high-temperature environment, hence is an element desired to be added in a large content if such an addition is possible, and is required to be added in a content of 3.5% or more. However, when the content of Ni is increased, the function of decreasing the Ms point is large. Consequently, when Ni is added in a large content, despite cooling of the austenitic phase stable at high temperatures, the transformation into martensite does not occur and a large amount of ⁇ -phase remains as the retained ⁇ -phase at normal temperature. Herewith, the strength of the stainless steel is drastically deteriorated.
  • a small amount of the retained ⁇ -phase has a small effect on the strength deterioration of the stainless steel, and is preferable for the purpose of ensuring high toughness.
  • the reduction of the content of Mn or the content of N is effective.
  • the content of Ni is set at 3% or more and less than 5%.
  • the preferable lower limit of Ni content is 3.6% and the more preferable lower limit is 4.0%.
  • the preferable upper limit ofNi content is 4.9% and the more preferable upper limit is 4.8%.
  • Al is an element that is necessary for deoxidization.
  • the content of Al is less than 0.001 %, the effect of Al is not sufficient, and when the content of Al exceeds 0.1 %, the amount of ferrite is increased to deteriorate the strength. Accordingly, the range of the content of Al is set at from 0.001 % to 0.1 %.
  • O oxygen
  • Oxgen is an element that deteriorates the toughness and the corrosion resistance, and hence it is preferable to reduce the content of O.
  • the symbols of elements in formula (1) respectively represent the contents (unit: mass%) of the elements in the steel.
  • the increase of the contents of Cr, Mo, Ni and Cu enables to improve the corrosion resistance; however, the addition of these elements in predetermined amounts or more decreases the Ms point and stabilizes the retained ⁇ -phase. Consequently, the strength of the stainless steel pipe is drastically deteriorated.
  • the ranges of the contents of Cr, Mo, Ni and Cu are defined as described above. Additionally, the present inventors have discovered that it is necessary to limit the content of Mn and the content of N for the purpose of sufficiently improving the strength of the stainless steel pipe while the respective contents of Cr, Mo, Ni and Cu are being limited within the above-described ranges.
  • the present inventors have examined in detail how the strength is varied when the content of Mn and the content of N are varied in a stainless steel in which the contents of Cr, Mo, Ni and Cu are respectively close to the upper limit values of the above-described ranges. Specifically, the present inventors have examined in detail how the strength is varied when the content of Mn and the content ofN are varied in a stainless steel which contains C: 0.01%, Cr: 17.5%, Mo: 2.5%, Ni: 4.8% and Cu: 2.5%. The results thus obtained are shown in Figure 1 . It is to be noted that the stainless steel used for the examination was prepared by applying heating at 980°C for 15 minutes, and subsequent quenching by water-cooling and subsequent tempering.
  • the symbol O refers to the cases where a yield strength (yield stress: YS) of 861 MPa or more was ensured under the tempering conditions of 500°C or higher and 30 minutes
  • the symbol ⁇ refers to the cases where YS was less than 861 MPa even under the tempering conditions of 500°C or higher and 30 minutes and even under the tempering conditions of lower than 500°C and 30 minutes.
  • the stainless steel having the above-described base composition has a yield strength of 861 MPa (125 ksi) or more when the stainless steel satisfies the above-described formula (1). Therefore, the present inventors limited the content of Mn and the content of N to the range satisfying above-described formula (1). Consequently, the strength of the stainless steel has been enabled to be sufficiently improved. It is to be noted that when the content of Mn exceeds 1%, the toughness is deteriorated, and hence the content of Mn is set at 1% or less irrespective of the content of N. On the other hand, when the content of N exceeds 0.05%, the precipitation of nitride of Cr is increased in amount to deteriorate the corrosion resistance, and hence the content ofN is set at 0.05% or less irrespective of the content of Mn.
  • Ca and B are elements to be optionally added.
  • the stainless steel according to the present invention takes a two-phase micro-structure composed of ferrite and austenite, and hence depending on the hot working conditions, flaws and defects may be produced on the stainless steel pipe.
  • the content of Ca exceeds 0.01 %, the amounts of inclusions are increased to deteriorate the toughness of the stainless steel pipe.
  • carbo-borides of Cr are precipitated in the crystal grain boundary to deteriorate the toughness of the stainless steel pipe.
  • the preferable contents of Ca and B are each set at 0.01% or less. It is to be noted that the above-described effects of Ca and B become remarkable when the content of Ca is 0.0003% or more, or when the content of B is 0.0002% or more. Accordingly, when one or more of Ca and B are included for the purpose of improving the pipe workability, the content of Ca is set more preferably in a range from 0.0003% to 0.01% and the content of B is set more preferably in a range from 0.0002% to 0.01%. In this connection, the upper limit of the total content of Ca and B is preferably 0.01% or less.
  • V, Ti, Zr, Nb 0.3% or less
  • V, Ti, Zr and Nb are elements to be optionally added.
  • the inclusion of one or more of V, Ti, Zr and Nb results in the production of carbo-nitrides in the stainless steel, and the precipitation effect and the grain refining effect improve the strength and the toughness.
  • the preferable content of each of V, Ti, Zr and Nb is set at 0.3% or less. It is to be noted that the above-described effects of V, Ti, Zr and Nb become remarkable when the content of any of these elements is 0.003% or more.
  • V, Ti, Zr and Nb are included for the purpose of further improving the strength and the toughness of the stainless steel, it is more preferable to set the content of each of these elements in a range from 0.003% to 0.3%.
  • the upper limit of the total content of V, Ti, Zr and Nb is preferably 0.3% or less.
  • the metal micro-structure becomes, at normal temperature, a metal micro-structure that contains 10% or more of a ferritic phase by volume fraction. It is to be noted that when the content of the ferritic phase in the stainless steel exceeds 40% by volume fraction, it becomes difficult to ensure a high strength. Accordingly, the content of the ferritic phase is set at from 10 to 40% by volume fraction.
  • the volume fraction of the ferritic phase can be calculated, for example, by the method in which the ground stainless steel is subjected to etching with a mixed solution of aqua regia and glycerin, and then the area proportion of the ferritic phase is measured by the point counting method.
  • the retained ⁇ -phase exerts only a small effect on the strength deterioration of the stainless steel and drastically improves the toughness.
  • the upper limit value of the content of the retained ⁇ -phase is set at 10% by volume fraction.
  • the volume fraction of the retained ⁇ -phase can be measured, for example, by an X-ray diffraction method. It is to be noted that for the purpose of improving the toughness of the stainless steel according to the present invention, the retained ⁇ -phase is preferably present in a volume fraction of 1.0% or more.
  • the metal micro-structure other than the ferritic phase and the retained ⁇ -phase is mainly composed of the tempered martensitic phase.
  • the martensitic phase is included in a volume fraction of 50% or more. It is to be noted that, in addition to the martensitic phase, carbides, nitrides, borides, Cu phases and the like may be present.
  • the production method of the stainless steel pipe according to the present invention is not particularly limited and is only required to satisfy the above-described individual requirements.
  • a billet of the stainless steel having the above-described alloy composition is produced.
  • a steel pipe is produced from the billet according to the process for producing a common seamless steel pipe.
  • a tempering treatment or a quenching-tempering treatment is performed.
  • the stainless steel pipes of the sample Nos. 1 to 31 having the metal micro-structures shown in Table 2 were prepared. Specifically, each of the steel types A to Z, a and b of stainless steel materials was melted, and heated at 1250°C for 2 hours; thereafter, by forging, a round billet was prepared for each of the steel types. Next, each of the round billets was maintained under heating at 1100°C for 1 hour, and thereafter a stainless steel pipe of 125 mm in diameter and 10 mm in wall thickness was prepared by piercing with a piercing mill for laboratory use.
  • each of the stainless steel pipes was heated at 980°C to 1200°C for 15 minutes and then water-cooled (quenching), and additionally, tempered at 500°C to 650°C to thereby regulate the metal micro-structure and the strength.
  • the details of the quenching conditions and the tempering conditions for each of the stainless steel pipes are shown in Table 2. It is to be noted that for each of the steel types H, P and N, two different types of heat treatments were conducted, and thus two stainless steel pipes having different metal micro-structures (the sample Nos. 8, 14, 16, and 29 to 31 in Table 2) were prepared.
  • the steel types A to R in Table 1 are the stainless steel materials in each of which the chemical composition was within the ranges defined in the present invention.
  • the steel types S to Z, a and b are the stainless steel materials of Comparative Examples in each of which the chemical composition deviated from the ranges defined in the present invention.
  • the stainless steel pipes of the sample Nos. 1 to 18 are the stainless steel pipes of Examples in each of which the chemical composition and the metal micro-structure were within the ranges defined in the present invention
  • the stainless steel pipes of the sample Nos. 19 to 31 are the stainless steel pipes of Comparative Examples in each of which the chemical composition or the metal micro-structure deviated from the ranges defined in the present invention.
  • the volume fraction of the ferritic phase were calculated by the method in which each of the ground stainless steels (specimens) was subjected to etching with a mixed solution of aqua regia and glycerin, and then the area proportion of the ferritic phase was measured by the point counting method. Additionally, the volume fraction of the retained ⁇ -phase was measured with an X-ray diffraction method. In Table 2, the results of the below-described tensile test and four-point bending corrosion test are also shown.
  • the specimens for performing the tensile test and the four-point bending corrosion test were sampled.
  • the tensile test specimens round rod tensile test specimens each having a diameter of 4 mm and a length of 20 mm in the parallel portion were sampled along the lengthwise direction of each of the stainless steel pipes. The tensile test was performed at normal temperature, and the yield strength (yield stress) was measured.
  • the stress corrosion cracking test in a high-temperature carbonic acid gas environment and the sulfide stress cracking test in an environment of a trace of hydrogen sulfide were performed.
  • Each of the four-point bending tests was performed according to the following guidelines. It is to be noted that the four-point bending test was performed for the specimens of the sample Nos. 1 to 18, 22, 25 and 26 (see Table 2).
  • the strength increase due to the precipitation strengthening was not sufficient, and no sufficient yield strength was obtained.
  • the stainless steel (see the steel type b in Table 1) of the sample No. 28 in which the content of Ni was less than the defined range of the present invention the ferritic phase was increased in amount, and consequently no sufficient yield strength was obtained.
  • the metal micro-structure (the volume fraction of the ferritic phase or the volume fraction of the retained ⁇ -phase) deviated from the defined range of the present invention, no sufficient strengths were obtained.
  • the quenching temperature was 1200°C and the quenching was performed from the region where the ⁇ -ferrite was stable. It is inferred that consequently the content of ferrite was increased.
  • the tempering temperature was the ferrite-austenite two-phase region temperature, and consequently, the retained austenite was increased in amount. From this fact, it is seen that the regulation of the metal micro-structure of the stainless steel carried out through heat treatment so that the metal micro-structure falls within the range of the present invention improves the yield strength.
  • the four-point bending test was performed for the stainless steels of the sample Nos. 1 to 18 which are Examples of the present invention and was performed for the stainless steels of the sample Nos. 22, 25 and 26, for each of which a predetermined strength had been obtained, of the stainless steels of Comparative Examples.
  • each of the stainless steels of the sample Nos. 1 to 18 which are Examples of the present invention has a high strength and additionally, an excellent corrosion resistance capable of sufficiently preventing the stress corrosion cracking in the high-temperature carbonic acid gas and the sulfide stress cracking at normal temperature.
  • the stainless steel pipe according to the present invention can be suitably used in various oil wells and gas wells.
  • Figure 1 is a graph showing the strength variation observed when the content of Mn and the content of N were varied in a stainless steel having a base composition of C: 0.01 %, Cr: 17.5%, Mo: 2.5%, Ni: 4.8% and Cu: 2.5%.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
  • Rigid Pipes And Flexible Pipes (AREA)
EP09823629.2A 2008-10-30 2009-10-28 Tuyau en acier inoxydable à haute limite élastique présentant une résistance élevée à la corrosion fissurante en présence d'hydrogène sulfuré et une résistance à la corrosion en présence de dioxyde de carbone à haute température Active EP2341161B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2008279014 2008-10-30
PCT/JP2009/068518 WO2010050519A1 (fr) 2008-10-30 2009-10-28 Tuyau en acier inoxydable à haute limite élastique présentant une résistance élevée à la corrosion fissurante en présence d'hydrogène sulfuré et une résistance à la corrosion en présence de dioxyde de carbone à haute température

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EP2341161A1 true EP2341161A1 (fr) 2011-07-06
EP2341161A4 EP2341161A4 (fr) 2014-07-02
EP2341161B1 EP2341161B1 (fr) 2015-09-30

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US (1) US8608872B2 (fr)
EP (1) EP2341161B1 (fr)
JP (1) JP4761008B2 (fr)
CN (1) CN102203309B (fr)
AR (1) AR073884A1 (fr)
AU (1) AU2009310835B2 (fr)
BR (1) BRPI0919892B1 (fr)
CA (1) CA2733649C (fr)
ES (1) ES2553759T3 (fr)
MX (1) MX2011004528A (fr)
RU (1) RU2459884C1 (fr)
WO (1) WO2010050519A1 (fr)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2832881A4 (fr) * 2012-03-26 2016-03-09 Nippon Steel & Sumitomo Metal Corp Acier inoxydable pour puits de pétrole et tuyau en acier inoxydable pour puits de pétrole
EP3042968A4 (fr) * 2013-09-04 2016-08-31 Jfe Steel Corp Procédé de fabrication de tuyau en acier inoxydable à haute résistance et tuyau en acier inoxydable à haute résistance
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EP2832881A4 (fr) * 2012-03-26 2016-03-09 Nippon Steel & Sumitomo Metal Corp Acier inoxydable pour puits de pétrole et tuyau en acier inoxydable pour puits de pétrole
EP3042968A4 (fr) * 2013-09-04 2016-08-31 Jfe Steel Corp Procédé de fabrication de tuyau en acier inoxydable à haute résistance et tuyau en acier inoxydable à haute résistance
US10151012B2 (en) 2013-09-04 2018-12-11 Jfe Steel Corporation High-strength stainless steel pipe
US10745774B2 (en) 2013-10-31 2020-08-18 Jfe Steel Corporation Ferrite-martensite dual-phase stainless steel and method of manufacturing the same
EP3246418A4 (fr) * 2015-01-15 2017-11-22 JFE Steel Corporation Tube d'acier inoxydable sans soudure pour puits de pétrole, et son procédé de fabrication
US11193179B2 (en) 2015-01-15 2021-12-07 Jfe Steel Corporation Seamless stainless steel pipe for oil country tubular goods and method of manufacturing the same
EP3333276A4 (fr) * 2015-08-04 2019-01-09 Nippon Steel & Sumitomo Metal Corporation Acier inoxydable et matériau en acier inoxydable pour puits de pétrole
WO2021084025A1 (fr) 2019-10-31 2021-05-06 Deutsche Edelstahlwerke Specialty Steel Gmbh & Co. Kg Acier résistant à la corrosion et à durcissement par précipitation, procédé de production d'un composant d'acier, et composant d'acier
EP3850114A1 (fr) * 2019-10-31 2021-07-21 Deutsche Edelstahlwerke Specialty Steel GmbH & Co.KG Acier résistant à la corrosion et à durcissement par précipitation, procédé de production d'un composant d'acier, et composant d'acier

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US20110226378A1 (en) 2011-09-22
US8608872B2 (en) 2013-12-17
AR073884A1 (es) 2010-12-09
RU2459884C1 (ru) 2012-08-27
EP2341161B1 (fr) 2015-09-30
EP2341161A4 (fr) 2014-07-02
WO2010050519A1 (fr) 2010-05-06
BRPI0919892B1 (pt) 2021-01-26
CN102203309B (zh) 2013-06-19
BRPI0919892A2 (pt) 2017-11-14
CN102203309A (zh) 2011-09-28
MX2011004528A (es) 2011-05-24
CA2733649A1 (fr) 2010-05-06
JP4761008B2 (ja) 2011-08-31
CA2733649C (fr) 2016-05-10
AU2009310835A1 (en) 2010-05-06
ES2553759T3 (es) 2015-12-11
AU2009310835B2 (en) 2012-09-06
JPWO2010050519A1 (ja) 2012-03-29

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